Silicon carbide semiconductor device and manufacturing method therefor

ABSTRACT

With a view to preventing increases in forward voltage due to a change with the lapse of time of a bipolar semiconductor device using a silicon carbide semiconductor, a buffer layer, a drift layer and other p-type and n-type semiconductor layers are formed on a growth surface, which is given by a surface of a crystal of a silicon carbide semiconductor having an off-angle θ of 8 degrees from a (000-1) carbon surface of the crystal, at a film growth rate having a film-thickness increasing rate per hour h of 10 μm/h, which is three times or more higher than conventional counterparts. The flow rate of silane and propane material gases and dopant gases is largely increased to enhance the film growth rate.

TECHNICAL FIELD

The present invention relates to a silicon carbide bipolar semiconductordevice suitable for control of large currents.

BACKGROUND ART

Wide-gap semiconductor materials including silicon carbide (SiC) havesuch excellent characteristics as their high dielectric breakdown fieldstrengths, which are about ten times higher than that of silicon (Si),and thus have been drawing attention as materials suitable for highwithstand voltage bipolar power semiconductor devices having highwithstand reverse voltage characteristics.

Bipolar semiconductor devices such as pin (Positive Intrinsic Negative)diodes, bipolar transistors, GTO (Gate Turn-Off Thyristor) and GCT(Gate-Commutated Thyristor), although high in built-in voltage ascompared with unipolar semiconductor devices such as Schottky diode andMOSFET, yet have a characteristic that their on-resistance is largelydecreased by conductivity modulation of the drift layer due to minoritycarrier injection. Accordingly, in high-voltage, large-current regionsfor power use or the like, bipolar semiconductor devices are used with aview to reducing losses. These bipolar semiconductor devices, when madefrom SiC, are enabled to implement far more excellent performance,compared with devices of Si. For example, a pin diode having a highwithstand voltage of 10 kV and made from SiC has a forward voltageamounting to about one third that of Si pin diodes. The SiC pin diodeshows a high-speed inverse recovery time, which represents operatingspeed at a turn-off, amounting to about 1/20 or less of that of the Sipin diode. Also, the SiC pin diode shows a power loss amounting to about⅕ or less of that of the Si pin diode, greatly contributing to energysaving. In addition to SiC pin diodes, SiC npn transistors, SiC SIAFETs,SiC SIJFETs and the like have been developed as well, and similar powerloss reduction effects have been reported (e.g., non-patent document 1).Otherwise, SiC GTOs using a p-type semiconductor layer of inversepolarity as a drift layer have also been developed (e.g., non-patentdocument 2).

A {0001} surface, which represents a set plane of SiC crystal, includesa (0001) silicon surface 1 and a (000-1) carbon surface 2, which areindividual surfaces, as shown in a perspective view of SiC crystal ofFIG. 7. In this case, a parenthesized symbol ‘−’ represents a negativesign, which is referred to as polarity. The (0001) silicon surface 1 isa surface in which the crystal is terminated by silicon (Si). The(000-1) carbon surface 2 is a surface in which the crystal is terminatedby carbon (C). Nitrogen (N), which is an N-type dopant, is incorporatedinto the SiC crystal to substitute carbon (C) in most cases. The (0001)silicon surface 1 terminated by silicon is smaller in the quantity ofsurface-appearing carbon than the (000-1) carbon surface 2 terminated bycarbon. Therefore, substitution of carbon into nitrogen (N) issuppressed so that a high-purity epitaxial layer can be obtained. Onaccount of this, most of study reports relating to epitaxial growth ofSiC are associated with the (000-1) silicon surface 1.

In SiC epitaxial growth, the CVD (Chemical Vapor Deposition) process,which allows easier control of the growth rate and the purity of theepitaxial layer, is used. However, since the CVD process employshydrogen as the carrier gas, separation of carbon (C) from the growthsurface occurs during the growth, causing the growth rate to besuppressed. Thus, the normal growth rate is 5 to 10 μm/h.

For fabrication of the conventional bipolar semiconductor device withSiC, for example, n-type 4H-SiC which has been formed so as to have asurface la whose off-angle θ from the (0001) silicon surface 1 is 8degrees is used for the substrate. In the term ‘4H’, numeral ‘4’represents a crystal structure in which atomic layers are of afour-layer cycle, and ‘H’ refers to hexagonal crystal. On thissubstrate, a SiC drift layer for relaxation of electric field in voltageapplication is formed by epitaxial growth at a growth rate of 5 to 10μm/h by using CVD process.

Non-patent document 1: Hiroyuki MATSUNAMI (editor and writer),“Semiconductor SiC technology and applications,” edited and written bypp. 218-221, Nikkan Kogyo Shimbunsha.

Non-patent document 2: “A. K. Agarwal et. al, Materials Science ForumVolume 389-393, 2002, pp. 1349-1352.

DISCLOSURE OF THE INVENTION

In the conventional bipolar semiconductor device obtained in this way,as reported in Materials Science Forum Vols. 389-393 (2002), pp.1259-1264, a phenomenon of a change with the lapse of time appears afterenergizing a new bipolar semiconductor device, the forward voltageincreases with the lapse of time (operating time). This phenomenon iscalled “forward voltage deterioration.” When a new bipolar semiconductordevice is subjected to one-hour forward conduction with a currentdensity of 100 A/cm², a forward voltage difference ΔVf at the currentdensity of 100 A/cm² between a time point immediately after the start ofconduction and another time point after one-hour conduction represents adegree of the forward voltage deterioration.

The forward voltage deterioration phenomenon occurs due to lineardefects which are called basal plane dislocations and which propagatefrom the substrate to the drift layer. With this basal plane dislocationtaken as a starting point, planar faults called stacking faults occur inthe drift layer, causing the drift layer to be highly resistive with theresult that the current does not easily flow.

In the case of conventional pin diodes, while the forward voltage at theforward current density of 100 A/cm² was 3.5 V in early stages of theuse, it increases to 20 V after one-hour conduction at a current densityof 100 A/cm², the forward voltage difference ΔVf being about 16.5 V.This causes a considerable increase in power loss inside the device sothat the device could be broken by heat generated inside the device. SiCbipolar devices, although having greatly excellent initialcharacteristics as comprised with Si device, are considerably low inreliability because of the forward voltage deterioration. Therefore, ithas been difficult to implement inverters or other power conversionunits which are capable of elongated operating time, low in power lossand high in reliability.

An object of the present invention is to provide a semiconductor devicewhich has such high reliability that the forward voltage difference ΔVfrepresenting forward voltage deterioration is not more than 1.0 V aswell as a manufacturing method therefor.

In order to achieve the above object, there is provided a bipolarsemiconductor device including:

a substrate in which a surface having a specified off-angle from a(000-1) carbon surface of a crystal of a first-conductive-type siliconcarbide semiconductor whose base material is silicon carbide, which is acompound of carbon and silicon, is formed; and

at least one drift layer which is formed on a crystal growth surface ofthe substrate at a specified formation rate with a first- orsecond-conductive-type silicon carbide semiconductor, where the surfaceof the substrate having the specified off-angle is taken as the crystalgrowth surface of the substrate.

According to the present invention, since the first- andsecond-conductive-type silicon carbide semiconductor layers are formedas described above, semiconductor layers less liable to basal planedislocation can be obtained. As a result, a pn junction diode which isless liable to forward voltage deterioration and long in service lifecan be obtained.

In one embodiment of the invention the bipolar semiconductor devicefurther includes at least one layer of a first- orsecond-conductive-type silicon carbide semiconductor formed on the driftlayer.

According to the embodiment, since the first- and second-conductive-typesilicon carbide semiconductor layers are formed as described above,semiconductor layers less liable to basal plane dislocation can beobtained. As a result, a pn junction diode or a bipolar transistor whichis less liable to forward voltage deterioration and long in service lifecan be obtained.

In one embodiment of the invention,

the substrate serves as a cathode and

the bipolar semiconductor device further includes a semiconductor layerwhich is formed on the drift layer and which is of asecond-conductive-type silicon carbide to serve as an anode.

According to the embodiment, since the first- and second-conductive-typesilicon carbide semiconductor layers are formed as described above,semiconductor layers less liable to basal plane dislocation can beobtained. As a result, a pn junction diode which is less liable toforward voltage deterioration and long in service life can be obtained.

Also, there is provided a bipolar semiconductor device including:

a substrate which is to serve as a collector and in which a surfacehaving a specified off-angle from a (000-1) carbon surface of a crystalof a first-conductive-type silicon carbide semiconductor whose basematerial is silicon carbide, which is a compound of carbon and silicon,is formed;

a drift layer which is formed on a crystal growth surface of thesubstrate at a specified film growth rate by epitaxial growth of afirst-conductive-type silicon carbide, where the surface of thesubstrate having the specified off-angle is taken as the crystal growthsurface of the substrate;

a second-conductive-type base layer formed on the drift layer; and

a first-conductive-type emitter layer formed on part of the base layer.

According to the bipolar semiconductor device, since the first- andsecond-conductive-type silicon carbide semiconductor layers are formedas described above, semiconductor layers less liable to basal planedislocation can be obtained. As a result, an npn transistor which isless liable to forward voltage deterioration and long in service lifecan be obtained.

Also, there is provided a bipolar semiconductor device including:

a substrate which is to serve as a collector and in which a surfacehaving a specified off-angle from a (000-1) carbon surface of a crystalof a first-conductive-type silicon carbide semiconductor whose basematerial is silicon carbide, which is a compound of carbon and silicon,is formed;

a drift layer which is formed on a crystal growth surface of thesubstrate at a specified film growth rate by epitaxial growth of asilicon carbide, where the surface of the substrate having the specifiedoff-angle is taken as the crystal growth surface of the substrate;

a first-conductive-type grown layer formed on the drift layer;

a second-conductive-type emitter layer formed on thefirst-conductive-type grown layer;

a contact region formed by ion implantation into thefirst-conductive-type grown layer via a through hole formed in thesecond-conductive-type emitter layer; and

a gate electrode formed via an insulating film on thefirst-conductive-type grown layer and the second-conductive-type emitterlayer.

According to the bipolar semiconductor device, since the first- andsecond-conductive-type silicon carbide semiconductor layers are formedas described above, semiconductor layers less liable to basal planedislocation can be obtained. As a result, an IGBT (Insulated GateBipolar Transistor) which is less liable to forward voltagedeterioration and long in service life can be obtained.

In order to achieve the above object, there is provided a manufacturingmethod for a bipolar semiconductor device comprising the steps of:

forming a substrate by cutting a crystal of a first-conductive-typesilicon carbide semiconductor whose base material is silicon carbide,which is a compound of carbon and silicon, by a surface having aspecified angle with respect to a (000-1) carbon surface of the crystal;

forming a drift layer on a crystal growth surface of the substrate at aspecified film growth rate by epitaxial growth of afirst-conductive-type silicon carbide, where the surface of thesubstrate having the specified angle is taken as the crystal growthsurface; and

forming at least one layer of a first- or second-conductive-type siliconcarbide semiconductor on the drift layer.

According to the manufacturing method, the off-angle is within a rangeof 2 to 10 degrees, and the film growth rate by epitaxial growth ofsilicon carbide that is to serve as the drift layer has a film-thicknessincreasing rate per hour h is 10 μm/h or more.

Therefore, supersaturation on the growth surface can be decreased sothat propagation of the basal plane dislocation from the substrate tothe epitaxial film can be suppressed. As a result, the forward voltagedeterioration can be prevented.

According to the present invention, since the propagation of the basalplane dislocation in the semiconductor layers is suppressed, forwardvoltage deterioration can be prevented. That is, the forward voltagedifference ΔVf representing forward voltage deterioration can besuppressed to 1.0 V or less, so that a high-reliability bipolar devicecan be made up. With the use of such a high-reliability bipolar device,power conversion equipment, such as inverters, which are reduced inloss, capable of long-term operation and high in reliability can beimplemented.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a sectional view of a pn (pin) diode which is a FirstEmbodiment of the present invention;

FIG. 2 is a graph showing current-voltage characteristics of the pindiode of the First Embodiment of the invention at a start of energizingand one hour after the energizing;

FIG. 3 is a graph showing current-voltage characteristics of a pin diodeof the First Embodiment of the invention and a pin diode using a Sisurface substrate made for comparison before deterioration, i.e.immediately after the conduction, and after deterioration, i.e. afterthe one-hour conduction;

FIG. 4 is a sectional view of an npn bipolar transistor which is aSecond Example of the invention;

FIG. 5 is a sectional view of an IGBT which is a Third Embodiment of theinvention is formed;

FIG. 6 is a perspective view showing a crystal of silicon carbide fromwhich a substrate of the bipolar semiconductor device of the invention;

FIG. 7 is a perspective view showing a crystal of silicon carbide fromwhich a substrate of a conventional bipolar semiconductor device isformed.

Explanation of Reference Numerals:

-   1 (0001) silicon surface-   2 (000-1) carbon surface-   3 substrate-   22 buffer layer-   23 drift layer-   24 p-type junction layer-   25 p+type contact layer-   26 JTE-   27 thermal oxide film-   28 cathode electrode-   29 anode electrode-   29 a Ti layer-   29 b Al layer-   50 npn bipolar transistor-   51 substrate-   52 buffer layer-   53 drift layer-   54 p-type grown layer-   55 n-type grown layer-   56 guard ring-   57 contact region of base-   58 oxide-   59 collector electrode-   60 IGBT-   61 substrate-   62 buffer layer-   63 drift layer-   64 n-type grown layer-   65 p-type grown layer-   66 contact region-   66 a hole-   67 insulating film-   68 gate electrode-   68 a hole-   69 collector terminal-   70 pin junction diode

BEST MODE FOR CARRYING OUT THE INVENTION

Hereinbelow, an embodiment of the invention will be described in detail.In the description of crystal lattice orientations and lattice surfaces,the following symbols, which are well known in the related technicalfields, are used to represent lattice orientations and lattice surfaces.That is, an individual surface is expressed by (), and a set surface isby {}, where respective numerals are enclosed therein to representindividual surfaces. Also, whereas the negative index is represented byadding a “−” (bar) on a numeral in crystallography, it is impossible toadded a bar above a numeral by software designated by JPO (JapanesePatent Office) and therefore a negative sign is added before a numeralfor expression in this specification.

For suppression of the forward deterioration phenomenon, it is necessaryto suppress propagation of the basal plane dislocation from thesubstrate to the drift layer as described before.

As a technique for forming the drift layer by SiC, epitaxial growthprocess is commonly used as reported in, for example, Materials Scienceand Engineering, R20 (1997) pp. 125-166. The epitaxial growth processincludes, roughly, in two growth modes, step flow growth andtwo-dimensional nucleation growth.

The step flow growth is a growth along a direction parallel to a {0001}surface which is perpendicular to the growth axis of crystal, having atendency to take over information attributed to the crystal parallel tothe {0001} surface. The two-dimensional nucleation growth is a growthalong a direction perpendicular to the {0001} surface, having a tendencyto take over information attributed to the crystal orientedperpendicular to the {0001} surface and also causing a generating sourceof defects in crystal growth.

Therefore, in normal epitaxial growth, growth conditions are so set thatthe step flow growth progresses to some extent in order to obtainhigh-quality epitaxial film.

The basal plane dislocation is a dislocation present parallel to the{0001} surface and propagates along the same direction as the step flowgrowth. Accordingly, for suppression of the propagation of the basalplane dislocation, the step flow growth needs to be suppressed to suchan extent that the two-dimensional nucleation does not occur.

Which growth goes, the step flow or the two-dimensional nucleation,depends largely on the supersaturation in crystal surfaces. When thesupersaturation goes beyond a certain value (critical supersaturation),the two-dimensional nucleation growth goes. With the supersaturationunder the value, the step flow growth goes. Therefore, given a largecritical supersaturation, the two-dimensional nucleation is less likelyto occur.

For obtainment of a large critical supersaturation, the growth rate isincreased by, for example, increasing the feed amount of material gas,or by reducing the off-angle of the crystal to widen the terrace (flatportions) of a step present in crystal surfaces.

In the. SiC crystal shown in FIG. 6, the (000-1) carbon surface 2 islower in surface energy by one order, therefore smaller in criticalsupersaturation value by one to two orders, than the (0001) siliconsurface 1. As a result, its supersaturation becomes relatively smallerto a large extent.

For the (000-1) carbon surface 2, a step having a height equal to onemolecular layer (not shown) is rather often adopted, where the molecularlayer comprises a single Si—C layer. However, for the (0001) siliconsurface 1, steps having a height of two or four molecular layers areobserved. This shows that the terrace of the (000-1) carbon surface 2becomes narrower in width to about half that of the (0001) siliconsurface 1. As a result of this, the critical supersaturation value ofthe (000-1) carbon surface 2 is smaller than that of the (0001) siliconsurface 1.

The critical supersaturation of the (000-1) carbon surface 2 dependslargely on the growth rate, the degree of dependence being larger thanthe degree of dependence on the width of the terrace of the step.Accordingly, the critical supersaturation of the (000-1) carbon surface2 can relatively be increased by enhancing the growth rate. As a resultof this, a step flow growth in which the two-dimensional nucleationgrowth can be suppressed and moreover propagation of the basal planedislocation can be suppressed can be achieved.

In the embodiment of the present invention, semiconductor layersincluding an n-type layer, a p-type layer and the like constituting theSiC bipolar semiconductor device are formed on a surface 2 a having aspecified off-angle θ relative to the (000-1) carbon surface 2 of theSiC crystal. The off-angle θ is determined for an optimum angle within arange of 2 to 10 degrees depending on the type of the semiconductordevice. According to an experiment by the inventors, successful resultswere obtained with an off-angle θ of about 8 degrees in the case of, forexample, a pin diode. For an IGBT, successful results were obtained withan off-angle θ of about 3.5 degrees. Furthermore, the growth rate of thesemiconductor layers is set faster than ordinary ones. The growth rateis desirably so set that the thin-film increasing amount per hour (h)becomes 10 μm/h or more. Depending on film growth conditions, the effectof the invention can be obtained even with film growth rates of 3 μm/hor more. In order to increase the growth rate, the amount of materialgas to be fed during the film growth process is increased to a largeextent.

Hereinbelow, preferred embodiments of the present invention areexplained with reference to FIGS. 1 to 6.

(First Embodiment)

FIG. 1 is a sectional view of a pn (pin) junction diode which is a FirstEmbodiment of a bipolar semiconductor device of the present invention.In this Embodiment, semiconductor layers to be described below areformed on an n-type (first conductive type) 4H SiC substrate 21 whosesurface orientation has an off-angle of 8 degrees from the (000-1)carbon surface. In the term “4H,” the character “H” means hexagonalcrystal and the numeral “4” means a crystal structure whose atomiclamination is four-layer cyclic. The C surface of the substrate 21 is asurface 2a having an off-angle θ of 8 degrees from the (000-1) carbonsurface 2 of SiC crystal of FIG. 6. The film growth rate for each layeris 15 μm/h, where the increasing rate of film thickness per hour (h) isfaster than in the conventional counterpart. Then, as described indetail below, n-type (first conductive type) 4H-SiC and p-type (secondconductive type) 4H-SiC are epitaxially grown one by one, by which anepitaxial pin junction diode 70 is fabricated. A primary junctionsurface of the p-type layer and an i layer (insulating layer), and aprimary junction surface (a surface extending in the horizontaldirection in FIG. 1) of the i layer and the n-type layer, are both a{0001} surface.

For comparison with the epitaxial pin junction diode 70 of thisEmbodiment, the following one was fabricated as a comparative pinjunction diode. That is, on an n-type 4H SiC surface 1 a (hereinafter,referred to as Si surface) having an off-angle θ of 8 degrees from the(0001) silicon surface 1 shown in FIG. 7, a pin junction diode forcomparison use is fabricated by making n-type 4H-SiC and p-type 4H-SiCepitaxially grown one by one at a growth rate having a film-thicknessincreasing rate per hour of 5 μm/h. The film growth rate of 5 μm/h is acommon rate for manufacturing process of pin diodes. The pin junctiondiode of this Embodiment and the pin junction diode for comparison useare identical in size and configuration of their junction portion.

The n-type substrate 21 was fabricated by slicing an ingot grown by amodified Rayleigh method at an off-angle 0 of 8 degrees, followed byspecular polishing. The substrate 21 was determined by the Hall effectmeasuring method to have a carrier density of 8×10¹⁸ cm⁻³ and athickness of 400 μm. On the substrate 21 serving as a cathode, anitrogen-doped n-type SiC layer (n-type grown layer) and analuminum-doped p-type SiC layer (p-type grown layer) are formed one byone in epitaxial growth by CVD process. By the n-type grown layer, ann-type buffer layer 22 and an n-type drift layer 23 shown in FIG. 1 areformed. The buffer layer 22 has a donor density of 7×10¹⁷ cm⁻³ and afilm thickness of 10 μm. The buffer layer 22 is not necessarily requiredand not formed in some cases. The drift layer 23 has a donor density ofabout 5×10¹⁵ cm⁻³ and a film thickness of 40 μm. On the drift layer 23,a p-type junction layer 24 serving as an anode and a p⁺-type contactlayer 25 were formed one by one by the p-type grown layer. The p-typejunction layer 24 has an acceptor density of 5×10¹⁷ cm⁻³ and a filmthickness of 1.5 μm. The p⁺-type contact layer 25 has an acceptordensity of 1×10¹⁸ cm⁻³ and a film thickness of 0.5 μm. Processingconditions for the buffer layer 22, the drift layer 23, the p-typejunction layer 24 and the p⁺-type contact layer 25 to be formed oneafter another on the C surface of the substrate 21 are as follows.

Processing conditions for fabrication of the pin junction diode 70 ofthis Embodiment are explained in detail below. Silane (SiH₄) and propane(C₃H₈) are used as material gases. Nitrogen (N₂) and trimethylaluminum(Al(CH₃)₃) are used as dopant gases. Further, hydrogen (H₂) is used asthe carrier gas. Flow rate of each gas is expressed in sccm (standard ccper minute) or slm (standard liter minute). Pressure is expressed in kPa(kilo Pascal) In the following description, a numerical valueparenthesized and added after the name of each gas represents a flowrate. The substrate 21 is kept at a temperature of 1550° C., and theinterior of the processing chamber is kept at a pressure of 5.6 kPa.

In a step for forming the buffer layer 22 on the C surface of thesubstrate 21, silane (30 sccm), propane (12 sccm), nitrogen (30 sccm)and hydrogen (10 slm) are fed. Processing time for this step is 40minutes.

In a step for forming the drift layer 23, silane (30 sccm), propane (12sccm), nitrogen (0.2 sccm) and hydrogen (10 slm) are fed. Processingtime for this step is 160 minutes.

In a step for forming the p-type junction layer 24, silane (30 sccm),propane (12 sccm), trimethylaluminum (15 sccm) and hydrogen (10 slm) arefed. Processing time for this step is 6 minutes.

In a step for forming the p⁺-type contact layer 25, silane (30sccm),propane (12sccm), trimethylaluminum (30sccm) and hydrogen (10 slm) arefed. Processing time for this step is 2 minutes.

By the processing shown above, a SiC epitaxial wafer for the pinjunction diode of this Embodiment is made up.

Next, processing conditions. for fabrication of the pin diode forcomparative use are described. Since its layers to be formed on the Sisurface of the substrate are substantially similar in structure to thoseof this Embodiment shown in FIG. 1, same reference numerals are used inthe description. The substrate is kept at a temperature of 1550° C., andthe interior of the processing chamber is kept at a pressure of 5.6 kPa.

In a step for forming the buffer layer 22 on the Si surface of thesubstrate, silane (10sccm), propane (3 sccm), nitrogen (10sccm) andhydrogen (10slm) are fed. Processing time for this step is 120 minutes.

In a step for forming the drift layer 23, silane (10sccm), propane (3sccm), nitrogen (0.07 sccm) and hydrogen (10slm) are fed. Processingtime for this step is 480 minutes.

In a step for forming the p-type junction layer 24, silane (10sccm),propane (3sccm), trimethylaluminum (5sccm) and hydrogen (10slm) are fed.Processing time for this step is 18 minutes.

In a step for forming the p⁺-type contact layer 25, silane (10sccm),propane (3sccm), trimethylaluminum (10sccm) and hydrogen (10slm) arefed. Processing time for this step is 6 minutes.

By the processing shown above, a SiC epitaxial wafer for the pinjunction diode for comparative use is made up.

In a comparison of processing conditions between the SiC epitaxial waferfor the pin junction diode of this Embodiment and the SiC epitaxialwafer for the pin junction diode for comparative use, flow rates of thematerial gas and the dopant gas in the processing conditions of thisEmbodiment are three times or more higher than those of the conventionalcounterpart, respectively. Also, the processing time for each layer inthis Embodiment is one third or less of the processing time of thecomparative counterpart. As shown above, this Embodiment ischaracterized by shortened processing time and enhanced film growthrate.

The SiC epitaxial wafer of this Embodiment and the SiC epitaxial waferfor comparative use are subjected to processing described below, bywhich the pin junction diode 70 of this Embodiment shown in the figureas well as the pin junction diode for comparative use having a similarstructure are made up.

First, both end portions of the SiC epitaxial wafer are removed byreactive ion etching (RIE) so as to be processed into a mesa structure.With CF₄ (carbon tetrafluoride) and O₂ used for RIE etching gas, the SiCepitaxial wafer was etched to a depth of about 2.5 μm by a plasmaprocessing apparatus under the conditions of a pressure of 5 Pa and ahigh-frequency power of 260 W. In this case, a SiO₂ film (thickness: 10μm) deposited by CVD was used as a mask material.

Next, for relaxation of electric field concentration at the bottomportion of the mesa formed by etching, a p-type JTE (JunctionTermination Extension) 26 having a width of 250 μm and a depth of 0.7 μmwas provided at mesa bottom portion. The JTE 26 was formed by Al ionimplantation. The energy for the Al ion implantation was varied in sixsteps between 30 to 450 keV, where the total dose amount was 1.2×10¹³cm⁻. The JTE 26 was designed for its formation so that the implantationlayer of the JTE 26 would become a box profile. The ion implantation wascarried out throughout at room temperature, where graphite (thickness: 5μm ) was used as the mask for the ion implantation. Heat treatment foractivation of implanted ions was carried out in an argon gas atmospherewith the conditions of 1700° C. and 3 minutes. After annealing, thermaloxide film 27 was formed as an overcoat by 3-hour wet oxidation at atemperature of 1200° C. Finally, a protective film 30 of polyimide resinwas formed on the thermal oxide film 27 for completion.

Next, Ni (thickness: 350 nm) was formed on the underside of thesubstrate 21 to provide a cathode electrode 28. On the p⁺-type contactlayer 25, films of Ti (titanium with thickness 350 nm) and Al (aluminumwith thickness 100 nm) were deposited, respectively, to provide an anodeelectrode 29. The anode electrode 29 was composed of a Ti layer 29 a andan Al layer 29 b. Finally, heat treatment was carried out at 1000° C.for 20 minutes, by which the cathode electrode 28 and the anodeelectrode 29 were made into ohmic electrodes, respectively. The pnjunction was sized as 2.6 mm in diameter, and generally circular-shaped.Although the p-type JTE 26 was formed by aluminum ion implantation inthis Embodiment, yet similar effects are achieved also by using ionimplantation of boron (B). Further, in the pin junction diode 70,junction surfaces (surfaces extending horizontally in the figure) of thebuffer layer 22, the drift layer 23, the p-type junction layer 24 andthe p⁺-type contact layer 25 are all parallel to the surface 2 a (inFIG. 6) having an off-angle of 8 degrees from the (000-1) carbon surface2.

Of the pin junction diode 70 of this Embodiment, the withstand voltageis 3500 V and the on-voltage is 3.6 V. The pin junction diode 70 wassubjected to one-hour conduction in the forward direction with a currentdensity of 100 A/cm², and current-voltage characteristics at roomtemperature immediately after the start of the conduction and after theone-hour conduction were measured with a curve tracer.

FIG. 2 is a graph showing forward current-voltage characteristics atroom temperature of the pin junction diode 70 of this embodiment formedon the surface 2 a of the n-type 4H SiC substrate (C surface) 21 whosesurface orientation has an off-angle θ of 8 degrees from the (000-1)carbon surface 2.

A forward voltage difference ΔVf between immediately after the start ofthe conduction and after one-hour conduction with a forward currentdensity of 100 A/cm² was not more than 0.1 V, hence almost nodifference. Therefore, in the graph of FIG. 2, the current-voltagecharacteristics are represented by one curve. As can be understood fromthis result, the pin junction diode 70 of this Embodiment showed almostno deterioration even after the one-hour conduction.

FIG. 3 is a graph showing current-voltage characteristics obtained by ameasurement of a comparative. pin junction diode, which was fabricatedin the same size for comparison with the pin junction diode 70 of thisEmbodiment, under the same conditions as in the pin junction diode 70 ofthis Embodiment. In FIG. 3, the curve of solid line shows acurrent-voltage characteristic immediately after the start of use(before deterioration) of the comparative pin junction diode. The curveof broken line shows a current-voltage characteristic after one-hour use(after deterioration). As can be understood from FIG. 3, the forwardvoltage difference ΔVf at a forward current density of 100 A/cm²(current value: 5.5 A) was 16.0 V. When the diode subjected to theconduction test was checked for photoluminescence emission which isknown as a means for checking defects in the art, a large number of 422nm emissions showing stacking faults were found in the comparative pinjunction diode using the Si surface. On the other hand, no emission ofstacking faults were found in the pin junction diode 70 using the Csurface of this Embodiment.

As described above, the pin junction diode of SiC of this Embodiment,because of its being almost free from occurrence of forward voltagedeterioration, becomes capable of long-term use, long in serve life.Since the pin junction diode is free from increases in on-resistance dueto forward voltage deterioration, a high-reliability pin junction diodewhich is free also from internal loss and which is capable ofmaintaining stable characteristics for long time can be obtained.

(Second Embodiment) FIG. 4 is a sectional view of an npn bipolartransistor 50 which is a Second Embodiment of the bipolar semiconductordevice of the invention. In this embodiment also, as shown in FIG. 6, ann-type 4H SiC substrate having a surface 2 a whose surface orientationhas an off-angle e of 8 degrees from the (000-1) carbon surface 2(hereinafter, referred to as C surface) is used. On this substrate,n-type 4H-SiC, p-type 4H-SiC and n-type 4H-SiC are successivelyepitaxially grown in this order with a film-thickness increasing rateper hour (h) of 15 μm/h, by which an npn bipolar transistor 50 wasfabricated.

Also, n-type 4H-SiC having a surface 1 a (hereinafter, referred to as Sisurface) whose off-angle θ from the (0001) silicon surface 1 shown inFIG. 7 was 8 degrees was used as the substrate for an npn bipolartransistor for comparison use. On this substrate, individual layers weregrown with a film-thickness increasing rate per hour (h) of 5 μm/h. Theprimary junction surface (a surface extending horizontally in thefigure) of the p and n layers is the {0001} surface.

A substrate 51 was fabricated by slicing an ingot grown by a modifiedRayleigh method at an off-angle θ of 8 degrees, followed by specularpolishing. The substrate 51 to serve as a collector, which was of then-type, was determined by the Hall effect measuring method to have acarrier density of 8×10¹⁸ cm⁻³ and a thickness of 400 μm. On the Csurface, a buffer layer 52 and a drift layer 53 of a nitrogen-dopedn-type SiC layer were grown by CVD process. On the drift layer 53, ap-type grown layer 54 of aluminum-doped p-type SiC, and an n-type grownlayer 55 of nitrogen-doped n-type SiC were grown one by one by epitaxialgrowth. The buffer layer 52 and the drift layer 53 serve as an n-typecollector layer. The buffer layer 52 has a donor density of 7×10¹⁷ cm⁻³and a film thickness of 10 μm. The drift layer 53 has a donor density ofabout 5×10¹⁵ cm⁻³ and a film thickness of 15 μm. Also, the p-type grownlayer 54 serving as a p-type base layer has an acceptor density of2×10¹⁷ cm⁻³ and a film thickness of 1 μm. The n-type grown layer 55 hasa donor density of 7×10¹⁷ cm⁻³ and a film thickness of 0.75 μm.Processing conditions for the buffer layer 52, the drift layer 53, thep-type grown layer 54 and the n-type grown layer 55 are as follows.

Processing conditions for fabrication of the npn bipolar transistor 50of this Embodiment are explained in detail below. Silane (SiH₄) andpropane (C₃H₈) are used as material gases. Nitrogen (N₂) andtrimethylaluminum (Al(CH₃)₃) are used as dopant gases. Further, hydrogen(H₂) is used as the carrier gas. A flow rate of each gas is expressed insccm (standard cc per minute) or slm (standard liter minute). Pressureis expressed in kPa (kilo Pascal). In the following description, anumerical value parenthesized and added after the name of each gasrepresents a flow rate. The substrate 51 is kept at a temperature of1550° C., and the interior of the processing chamber is kept at apressure of 5.6 kPa.

In a step for forming the buffer layer 52 on the C surface of thesubstrate 51, silane (30sccm), propane (12sccm), nitrogen (30sccm) andhydrogen (10slm) are fed. Processing time for this step is 40 minutes.

In a step for forming the drift layer 53, silane (30sccm), propane(12sccm), nitrogen (0.2 sccm) and hydrogen (10slm) are fed. Processingtime for this step is 60 minutes.

In a step for forming the p-type junction layer 54, silane (30sccm),propane (12sccm), trimethylaluminum (6 sccm) and hydrogen (10slm) arefed. Processing time for this step is 4 minutes.

In a step for forming the n-type grown layer 55, silane (30sccm),propane (12sccm), nitrogen (30sccm) and hydrogen (10slm) are fed.Processing time for this step is 3 minutes.

By the processing shown above, a SiC epitaxial wafer for the pinjunction diode of this Embodiment is made up.

Next, processing conditions for fabrication of the npn bipolartransistor for comparative use are described. Since its layers to beformed on the Si surface of the substrate are substantially similar instructure to those of this Embodiment shown in FIG. 4, same referencenumerals are used in the description. The substrate is kept at atemperature of 1550° C., and the interior of the processing chamber iskept at a pressure of 5.6 kPa.

In a step for forming the buffer layer 52 on the Si surface of thesubstrate, silane (10sccm), propane (3 sccm), nitrogen (10sccm) andhydrogen (10slm) are fed. Processing time for this step is 120 minutes.

In a step for forming the drift layer 53, silane (10sccm), propane(3sccm), nitrogen (0.07 sccm) and hydrogen (10slm) are fed. Processingtime for this step is 180 minutes.

In a step for forming the p-type grown layer 54, silane (10sccm),propane (3sccm), trimethylaluminum (2 sccm) and hydrogen (10slm) arefed. Processing time for this step is 12 minutes.

In a step for forming the n-type grown layer 55, silane (10sccm),propane (3sccm), nitrogen (10sccm) and hydrogen (10slm) are fed.Processing time for this step is 9 minutes.

By the processing shown above, a SiC epitaxial wafer for comparative useis made up. By subjecting the SiC epitaxial wafer of this Embodiment andthe comparative SiC epitaxial wafer to the processing described below,respectively, an npn bipolar transistor 50 shown in FIG. 4 and acomparative npn bipolar transistor similar in structure thereto are madeup.

First, the n-type grown layer 55 is etched by reactive ion etching (RIE)at a width of 10 μm, a depth of 0.75 μm and a pitch of 23 μm so that ann-type grown layer 55 to serve as an emitter is left. With CF₄ and O₂used for RIE etching gas, the grown layer was etched under theconditions of a pressure of 0.05 Torr and a high-frequency power of 260W. In this case, a SiO₂ film (thickness: 10 μm) deposited by CVD wasused as a mask material.

Next, for execution of device isolation in the base region, a mesastructure was formed by reactive ion etching (RIE). With CF₄ and O₂ usedfor RIE etching gas, the mesa structure was etched to a depth of about 1μm under the conditions of a pressure of 0.05 Torr and a high-frequencypower of 260 W. In this case, a SiO₂ film (thickness: 10 μm) depositedby CVD was used as a mask material.

In this embodiment, a guard ring 56 for relaxation of electric fieldconcentration at base end portions and a base contact region 57 wereformed by Al (aluminum) ion implantation of the same process. The basecontact region 57 is 3 μm wide with a spacing of 5 μm from the emitter,and the p-type guard ring 56 is 150 μm, where the depth of both is 0.5μm. The energy for the Al ion implantation in the formation of thep-type guard ring 56 or the base contact region 57 is 40 to 560 keV, andthe total dose amount is 1.0×10¹³ cm⁻². A SiO₂ film (thickness: 5 μm)formed by CVD was used as the mask for the ion implantation. The ionimplantation was carried out throughout at room temperature, and heattreatment for activation of implanted ions was carried out in an argongas atmosphere with a temperature of 1600° C. for 5 minutes. Afterannealing, thermal oxide film was formed by two-hour wet oxidation at atemperature of 1150° C., and further a SiO₂ film was deposited by CVD toform oxide film 58 of totally 2 μm.

Next, a collector electrode 59 was formed on the underside of thesubstrate 51. A base electrode 73 was formed in the base contact region57. Further, an emitter electrode 74 was formed by deposition of Ni onthe n-type grown layer 55. Subsequently, heat treatment was carried outat 1000° C. for 20 minutes, by which ohmic junctions were formed,respectively. Finally, the base electrode 73 and the emitter electrode74 were covered with Ti/Au electrodes, by which electrode terminals 75,76 were formed, respectively. The junction portion was sized as 3.2mm×3.2 mm. Although the guard ring 56 was formed by Al ion implantationin this Embodiment, yet similar effects are achieved also by using ionimplantation of boron (B). Further, in the npn bipolar transistor 50,junction surfaces (surfaces extending horizontally in the figure) of thesubstrate 51, the buffer layer 52, the drift layer 53, the p-type grownlayer 54 and the n-type grown layer 55 are all parallel to the surface 2a having an off-angle of 8 degrees from the (000-1) carbon surface 2.

Of the fabricated npn bipolar transistor 50, the withstand voltage was1400 V, the on-voltage was 8.0 mΩcm², and the maximum currentamplification factor was about 12. The npn bipolar transistor 50 wassubjected to one-hour conduction with a base current of 0.6 A and acollector current 7A (collector current density: 100 A/cm²), andcollector characteristics at room temperature before and after theconduction were measured with a curve tracer.

In the npn bipolar transistor 50 of this Embodiment, the on-resistancewas 8.0 mΩcm² both immediately after the start of the conduction andafter the one-hour conduction, hence almost no change in forwardvoltage.

The npn bipolar transistor of the comparative example was similarlysubjected to a conduction test with a collector current density of 100A/cm². The on-resistance of the comparative npn bipolar transistor atroom temperature was 8.0 mΩcm² immediately after the start of theconduction, but greatly increased to 15.0 mΩcm² after the one-hourconduction. Further, the maximum current amplification factor of thecomparative npn bipolar transistor was about 12 early in the conduction,but decreased to about 6 after the one-hour conduction.

In contrast to this, the maximum current amplification factor of the npnbipolar transistor of this Embodiment remain to be about 12 with almostno changes between immediately after the start of the conduction andafter the one-hour conduction. As shown above, the npn bipolartransistor of this Embodiment showed almost no occurrence of forwardvoltage deterioration even after the one-hour conduction test.

(Third Embodiment) A Third Embodiment relates to an IGBT (Insulated GateBipolar Transistor) which is a bipolar semiconductor device of the-present invention. FIG. 5 is a sectional view of an IGBT 60 of thisEmbodiment. In this Embodiment, a substrate 61 (hereinafter, referred toas C surface substrate) using n-type 6H SiC whose surface orientationhas an off-angle θ of 3.5 degrees from the (000-1) carbon surface 2 inFIG. 6 is prepared. On the substrate 61, three layers, i.e. a p-type6H-SiC layer, an n-type 6H-SiC layer and a p-type 6H-SiC layer, areepitaxially grown in this order with a film-thickness increasing rateper hour (h) of 15 μm/h, by which an IGBT 60 is fabricated as isexplained in detail below. The primary junction surface (a surfaceextending horizontally in the figure) of the p and n layers is the{0001} surface.

A comparative IGBT for comparison with the IGBT of this Embodiment isfabricated in the following way. A substrate (hereinafter, referred toas Si surface substrate) using n-type 6H SiC having a surface 1 a whosesurface orientation is an off-angle θ of 3.5 degrees from the (0001)silicon surface 1 in FIG. 7 is prepared. On this substrate, a p-type6H-SiC layer, an n-type 6H-SiC layer and a p-type 6H-SiC layer areformed successively at a film growth rate of 5 μm/h.

The substrate 61 was fabricated by slicing an ingot grown by a modifiedRayleigh method with a plane inclined by 3.5 degrees from the (000-1)carbon surface, followed by specular polishing. The substrate 61 toserve as a cathode, which was of the n-type and being 400 μm thick, wasdetermined by the Hall effect measuring method to have a carrier densityof 5×10¹⁸ cm⁻³. On this substrate, three layers, i.e. an aluminum-dopedp-type SiC layer, a nitrogen-doped n-type SiC layer and analuminum-doped p-type SiC layer, were grown successively by epitaxialgrowth by CVD process. The p-type SiC layer becomes a buffer layer 62and a drift layer 63 of FIG. 5. buffer layer 62 has an acceptor densityof 1×10¹⁷ cm⁻³ and a film thickness of 3 μm. The drift layer 63 has anacceptor density of about 5×10¹⁵ cm⁻³ and a film thickness of 15 μm. Ann-type grown layer 64 to be formed on the drift layer 63 has a donordensity of 2×10¹⁷ cm⁻³ and a film thickness of 2 μm. A p-type grownlayer 65 to be formed on the n-type grown layer 64 has an acceptordensity of 1×10¹⁸ cm⁻³ and a film thickness of 0.75 μm. Film growthconditions for the buffer layer 62, the drift layer 63, the n-type grownlayer 64 and the p-type grown layer 65 are as follows.

Processing conditions for fabrication of the IGBT of this Embodiment areexplained in detail below. Silane (SiH₄) and propane (C₃H₈) are used asmaterial gases. Nitrogen (N₂) and trimethylaluminum (Al(CH₃)₃) are usedas dopant gases. Further, hydrogen (H₂) is used as the carrier gas. Aflow rate of each gas is expressed in sccm (standard cc per minute) orslm (standard liter minute). Pressure is expressed in kPa (kilo Pascal).In the following description, a numerical value parenthesized and addedafter the name of each gas represents a flow rate. The substrate 61 iskept at a temperature of 1550° C., and the interior of the processingchamber is kept at a pressure of 5.6 kPa.

In a step for forming the buffer layer 62 on the C surface of thesubstrate 61, silane (30 sccm), propane (12 sccm), trimethylaluminum (3sccm) and hydrogen (10 slm) are fed. Processing time for this step is 12minutes.

In a step for forming the drift layer 63, silane (30 sccm), propane (12sccm), trimethylaluminum (0.15 sccm) and hydrogen (10 slm) are fed.Processing time for this step is 60 minutes.

In a step for forming the n-type grown layer 64, silane (30 sccm),propane (12 sccm), nitrogen (9 sccm) and hydrogen (10 slm) are fed.Processing time for this step is 8 minutes.

In a step for forming the p-type grown layer 65, silane (30 sccm),propane (12 sccm), trimethylaluminum (30 sccm) and hydrogen (10 slm) arefed. Processing time for this step is 3 minutes.

By the processing shown above, a SiC epitaxial wafer for the pinjunction diode of this Embodiment is made up.

Next, processing conditions for fabrication of the IGBT for comparativeuse are described. Since its layers to be formed on the Si surface ofthe substrate are substantially similar in structure to those of thisEmbodiment shown in FIG. 5, same reference numerals are used in thedescription. The substrate is kept at a temperature of 1550° C, and theinterior of the processing chamber is kept at a pressure of 5.6 kPa.

In a step for forming the buffer layer 62 on the Si surface of thesubstrate, silane (10 sccm), propane (3 sccm), trimethylaluminum (1sccm) and hydrogen (10 slm) are fed. Processing time for this step is 36minutes.

In a step for forming the drift layer 63, silane (10 sccm), propane (3sccm), trimethylaluminum (0.05 sccm) and hydrogen (10 slm) are fed.Processing time for this step is 180 minutes.

In a step for forming the n-type grown layer 64, silane (10 sccm),propane (3 sccm), nitrogen (3 sccm) and hydrogen (10 slm) are fed.Processing time for this step is 24 minutes.

In a step for forming the p-type grown layer 65, silane (10 sccm),propane (3 sccm), trimethylaluminum (10 sccm) and hydrogen (10 slm) arefed. Processing time for this step is 9 minutes.

By the processing shown above, a SiC epitaxial wafer for the comparativepin junction diode is made up. By subjecting the SiC epitaxial wafer ofthis Embodiment and the comparative SiC epitaxial wafer to theprocessing described below, respectively, an IGBT of this Embodimentshown in the figure and a comparative IGBT similar in structure theretoare made up.

Steps for fabricating the IGBT 60 shown in FIG. 5 from the resulting SiCepitaxial wafer are explained below.

First, a central portion of the p-type grown layer 65 is etched by RIEto provide a hole 66 a with use of photolithography process. Nitrogenions are implanted into the n-type grown layer 64 located at a bottomportion of the hole 66 a, by which a contact region 66 to serve as acollector is formed.

For formation of a gate region, the p-type grown layer 65 and the n-typegrown layer 64 are etched by RIE to form a hole 68 a (two in FIG. 5).Subsequently, for formation of a MOS structure on the wall surface ofthe hole 68 a, a SiO₂ film is deposited by CVD to form an insulatingfilm 67.

Ni is deposited in the collector region of the substrate 61 to provide acollector terminal 69. Also, an emitter electrode 79 is deposited in thecontact region 66. Next, heat treatment is carried out to form ohmicjunctions, respectively. Further, a Mo electrode is formed on theinsulating film 67 to provide a gate electrode 68.

Of the completed IGBT of this Embodiment and the comparative IGBT, thewithstand voltage is 900 V. Their on-resistance is 11RΩcm² and theircollector-emitter voltage is −14 V. With a gate voltage of −40 V appliedto the two IGBTs, one-hour conduction was carried out with a collectorcurrent of 1.4 A, and collector characteristics at room temperature atthe time of start of the conduction and after the one-hour conductionwere measured with a curve tracer. In the IGBT of this Embodiment, thecollector-emitter voltage was −14 V both immediately after the start ofthe conduction and after the one-hour conduction, hence almost nochange, making it found that there occurred no deterioration. In thecomparative IGBT using a Si surface substrate, the collector-emittervoltage immediately after the conduction was −14 V, while thecollector-emitter voltage after the one-hour conduction became as largeas −29 V.

In order to check the state of deterioration, the gate electrode 68 andthe emitter electrode 79 of the after-conduction IGBT were removed, andphotoluminescence emission of SiC was examined. While a large number ofemissions showing stacking faults were found in the after-conductionIGBT using the Si surface substrate, no emission of stacking faults werefound in the IGBT using the C surface substrate.

As described above, the bipolar semiconductor device of the presentinvention has been described based on three Embodiments. However, theinvention is not limited to the above Embodiments, but is applicablealso to various kinds of 4H-SiC bipolar semiconductor devices such asSIAFETs, SIJFETs, thyristors, GTOs, MCTs (Mos Controlled Thyristors),SiCGT (SiC Commutated Gate Thyristors), ESTs (Emitter SwitchedThyristors), and BRTs (Base Resistance Controlled Thyristors).Naturally, the invention can be modified and applied to various kinds of4H-SiC bipolar devices such as opposite-polarity devices (e.g., pnptransistors for npn transistors), and further applicable to SiC bipolardevices using 6H-SiC or other crystal structures.

INDUSTRIAL APPLICABILITY

The present invention can be used for SiC bipolar semiconductor deviceswhich are less liable to a change with the lapse of time even if usedfor elongated time.

1-12. (canceled)
 13. A bipolar semiconductor device including: asubstrate in which a surface having a specified off-angle from a (000-1)carbon surface of a crystal of a first-conductive-type silicon carbidesemiconductor whose base material is silicon carbide, which is acompound of carbon and silicon, is formed; and at least one drift layerwhich is formed on a crystal growth surface of the substrate at aspecified formation rate with a first- or second-conductive-type siliconcarbide semiconductor, where the surface of the substrate having thespecified off-angle is taken as the crystal growth surface of thesubstrate.
 14. The bipolar semiconductor device as claimed in claim 13,further including at least one layer of a first- orsecond-conductive-type silicon carbide semiconductor formed on the driftlayer.
 15. The bipolar semiconductor device as claimed in claim 13,wherein the substrate serves as a cathode and the bipolar semiconductordevice further includes a semiconductor layer which is formed on thedrift layer and which is of a second-conductive-type silicon carbide toserve as an anode.
 16. A bipolar semiconductor device including: asubstrate which is to serve as a collector and in which a surface havinga specified off-angle from a (000-1) carbon surface of a crystal of afirst-conductive-type silicon carbide semiconductor whose base materialis silicon carbide, which is a compound of carbon and silicon, isformed; a drift layer which is formed on a crystal growth surface of thesubstrate at a specified film growth rate by epitaxial growth of afirst-conductive-type silicon carbide, where the surface of thesubstrate having the specified off-angle is taken as the crystal growthsurface of the substrate; a second-conductive-type base layer formed onthe drift layer; and a first-conductive-type emitter layer formed onpart of the base layer.
 17. A bipolar semiconductor device including: asubstrate which is to serve as a collector and in which a surface havinga specified off-angle from a (000-1) carbon surface of a crystal of afirst-conductive-type silicon carbide semiconductor whose base materialis silicon carbide, which is a compound of carbon and silicon, isformed; a drift layer which is formed on a crystal growth surface of thesubstrate at a specified film growth rate by epitaxial growth of asilicon carbide, where the surface of the substrate having the specifiedoff-angle is taken as the crystal growth surface of the substrate; afirst-conductive-type grown layer formed on the drift layer; asecond-conductive-type emitter layer formed on the first-conductive-typegrown layer; a contact region formed by ion implantation into thefirst-conductive-type grown layer via a through hole formed in thesecond-conductive-type emitter layer; and a gate electrode formed via aninsulating film on the first-conductive-type grown layer and thesecond-conductive-type emitter layer.
 18. The bipolar semiconductordevice as claimed in claim 13, wherein the off-angle is within a rangeof 2 to 10 degrees.
 19. The bipolar semiconductor device as claimed inclaim 14, wherein the film that is to serve as a drift layer and that isformed by epitaxial growth of silicon carbide is formed at a film growthrate having a film-thickness increasing rate per hour h of 10 μm/h ormore.
 20. The bipolar semiconductor device as claimed in claim 13,further including a buffer layer formed between the substrate and thedrift layer.
 21. A manufacturing method for a bipolar semiconductordevice comprising the steps of: forming a substrate by cutting a crystalof a first-conductive-type silicon carbide semiconductor whose basematerial is silicon carbide, which is a compound of carbon and silicon,by a surface having a specified angle with respect to a (000-1) carbonsurface of the crystal; forming a drift layer on a crystal growthsurface of the substrate at a specified film growth rate by epitaxialgrowth of a first-conductive-type silicon carbide, where the surface ofthe substrate having the specified angle is taken as the crystal growthsurface; and forming at least one layer of a first- orsecond-conductive-type silicon carbide semiconductor on the drift layer.22. The bipolar semiconductor device manufacturing method as claimed inclaim 21 wherein the specified angle is within a range of 2 to 10degrees.
 23. The bipolar semiconductor device manufacturing method asclaimed in claim 21, wherein a film-thickness increasing rate per hour hin the step of forming the drift layer is 10 μm/h or more.
 24. Thebipolar semiconductor device manufacturing method as claimed in claim21, further comprising a step of: forming a buffer layer between thesubstrate and the drift layer.